Date post: | 05-Sep-2016 |
Category: |
Documents |
Upload: | chun-kai-wang |
View: | 215 times |
Download: | 0 times |
Electrochromic Nb-doped WO3 films: Effects of post annealing
Chun-Kai Wang a, Diptiranjan Sahu a,b,*, Sheng-Chang Wang c, Jow-Lay Huang a,d,e,**a Department of Materials Science and Engineering, National Cheng Kung University No. 1, Ta-Hsueh Road, Tainan City 701, Taiwan, ROC
b School of Physics, Materials Physics Research Institute and DST/NRF Centre of Excellence in Strong Materials, University of the Witwatersrand, Private Bag 3,
Wits 2050, Johannesburg, South Africac Department of Mechanical Engineering, Southern Taiwan University of Technology, Tainan 710, Taiwand Center for Micro/Nano Science and Technology, National Cheng Kung University, Tainan 701, Taiwan
e Research Center for Energy Technology and Strategy, National Cheng Kung University, Tainan 701, Taiwan
Received 21 October 2011; received in revised form 24 October 2011; accepted 21 November 2011
Available online 29 November 2011
Abstract
The Nb-doped WO3 films were deposited by e-beam co-evaporation method using ceramic WO3 targets and metal Nb slugs. The films were
analyzed by glancing incident angle X-ray diffraction (GIAXRD), UV/visible spectrophotometer, electrochemical cyclic voltammetry, X-ray
photoelectron spectroscopy (XPS). The as-prepared film is brown and amorphous in structure. The film has low transmission in optical visible
region. The XPS results indicate that the as-deposited film is non-stoichiometric. By applying a negative potential, the as-deposited film does not
show obvious electrochromic effect. However, the electrochromic properties of Nb-doped WO3 films are improved by post annealing treatment at
350, 400, and 450 8C in oxygen atmosphere. The Nb-doped WO3 films transform into crystalline structure and become transparent after post
annealing treatment. The energy band gap, optical modulation, and color efficiency increase with annealing temperature.
# 2011 Elsevier Ltd and Techna Group S.r.l. All rights reserved.
Keywords: Electrochromism; WO3; Annealing; E-beam evaporation
www.elsevier.com/locate/ceramint
Available online at www.sciencedirect.com
Ceramics International 38 (2012) 2829–2833
1. Introduction
The electrochromic materials possess the ability of
reversible and persistent change of optical properties by
double insertion/extraction of electrons and counter ions (H+,
Li+.) [1,2]. This unique property makes electrochromic
materials of great interest for application in different types
of optical devices, such as display, rear view mirror, and smart
windows [3–6]. Among diverse electrochromic materials,
tungsten oxide (WO3), which turns blue upon electrochemical
insertion and becomes transparent upon extraction, is by far the
most extensively studied materials prepared by vacuum
* Corresponding author at: School of Physics, Materials Physics Research
Institute and DST/NRF Centre of Excellence in Strong Materials, University of
the Witwatersrand, Private Bag 3, Wits 2050, Johannesburg, South Africa.
Tel.: +27 11 7176839/+886 6 2348188; fax: +27 11 7176879/+886 6 2763586.
** Corresponding author at: Department of Materials Science and Engineering,
National Cheng-Kung University No. 1, Ta-Hsueh Road, Tainan City 701,
Taiwan, ROC. Tel.: +27 11 7176839/+886 6 2348188;
fax: +27 11 7176879/+886 6 2763586.
E-mail addresses: [email protected] (D. Sahu),
[email protected] (J.-L. Huang).
0272-8842/$36.00 # 2011 Elsevier Ltd and Techna Group S.r.l. All rights reserve
doi:10.1016/j.ceramint.2011.11.054
evaporation [7–9], chemical vapor deposition [10], hydro-
thermal [11] sol–gel [12,13], sputtering [14,15] and electro-
deposition [16]. For a few years, there is an extensive study for
the improvement of the properties of tungsten oxide by addition
of enhanced dopant [17–23]. Some compounds, such as TiO2,
MoO3 and Nb2O5, are used to increase coloration efficiency,
cycling lifetime, or reaction kinetics. Bathe and Patil [21]
shows that the cycle stability, charge storage capacity, and
reversibility can be improved by addition of Nb2O5 into WO3
films. Avellaneda’s study [24] indicates the mixed Nb2O5–WO3
films have larger optical modulation in photochromic reaction.
Rougier et al. [19] showed that the W–Nb–O films possess the
property of color neutrality which is promising for building
application in reduced state. However, there are few studies on
the effect of post annealing on electrochromic Nb-doped WO3
films. In this study, we prepared Nb-doped WO3 films by
electron evaporation method and investigated the influence of
post annealing treatment on the electrochromic properties.
2. Experimental procedure
The Nb-doped WO3 films are prepared by electron beam co-
evaporation method. The deposition targets are ceramic WO3
d.
Fig. 1. SEM images of (a) as-deposited and heat-treated films at (b) 350, (c) 400, (d) 450 8C in O2 atmosphere.
C.-K. Wang et al. / Ceramics International 38 (2012) 2829–28332830
bulks and metal Nb slugs. Before deposition, the vacuum
chamber is evacuated to 1.07 � 10�4 Pa and the deposition
pressure is controlled at 6.67 � 10�5–2.67 � 10�4 Pa. After
deposition, the Nb-doped WO3 films are post annealed in O2
atmosphere at 350, 400, and 450 8C for 2 h.
The film crystal structure was examined by Rigaku DMAX
2500 diffractometer with Cu Ka radiation of wavelength
0.1542 nm. The film surface morphology was studied by Philips
XL40 field emission scanning electron microscopy (FE-SEM).
The optical transmittance spectrum was measured by Hitachi U-
2001 UV/Visible Spectrophotometer in the range of 300–
1100 nm. The composition distribution profile and surface
chemical state were inspected by X-ray photoemission spectro-
scopy (PHI 5000 VersaProbe). The X-ray excitation source is Al
Ka radiation of energy 1486.6 eV. The carbon 1s peak with
binding energy 284.6 eVis used to calibrate tungsten and niobium
binding energy. The cycling voltammogram tests were carried out
on VersaStat II Electrochemical Workstation with three electrodes
configuration. The counter and reference electrodes were
platinum and saturated calomel electrode (SCE). The electrolyte
was 0.1 M LiClO4/propylene carbonate (PC) solution.
3. Results and discussion
The thickness of the Nb-doped WO3 films deposited by
electron beam co-evaporation is about 350 nm. The as-
deposited film contains 27.79% W, 17.30% Nb, and 53.1%
O and the composition is well distribution, as examined by
XPS. Fig. 1 shows the morphology of Nb-doped WO3 films for
as-deposited state and the post annealed films at 350, 400,
450 8C in O2 atmosphere. It is observed that grain size increases
with annealing temperature.
Fig. 2 shows the GIAXRD patterns of Nb-doped WO3 films
at three different postannealing temperatures in O2 atmosphere.
The GIAXRD pattern of as-prepared film is amorphous
structure without any obvious diffraction peaks. After post
annealing process, a diffraction peak at 258 appears and the
peak intensity increases with post annealing temperature. It can
be explained by the fact that the electrochromic films have
crystallized by post annealing treatment. Compared to the
Bathe’s results [21], the GIAXRD patterns do not reveal the
formation of solid solution WNb2O8 even after annealing at
450 8C in O2 atmosphere. This difference may be caused due to
different preparation methods. Bathe prepared W–Nb–O films
by sol–gel method in which the chemical activity of precursor is
higher than that of atomic evaporation method. The as-
deposited Nb-doped WO3 film is deep brown color and the
optical transmittance is below 20%. The optical transmittance
of Nb-doping WO3 film is increased by post annealing process
in O2 atmosphere, as shown in Fig. 3. The optical transmittance
of Nb-doped WO3 increase gradually from as-deposited state to
400 8C post-annealed film and the optical transmittance of Nb-
doping WO3 film does not increase further even after post
annealing at 450 8C. The film color becomes transparent after
80706050403020
WO3
* *
450 oC
400 oC
Inte
nsity
(arb
. uni
ts)
2θ (degree)
as-deposited
350 oC
*ITO substrate
Fig. 2. The GIAXRD patterns of Nb-doping WO3 film after three different
postannealing temperatures in O2 atmosphere.
110010009008007006005004003000
10
20
30
40
50
60
70
80
90
100
Tran
smitt
ance
(%)
Wavelength (nm)
as-deposited 350 oC 400 oC 450 oC
Fig. 3. The optical transmittance spectra of Nb-doped WO3 films at as-
deposited state and after post annealing treatment at 350, 400, and 450 8Cin O2 atmosphere.
C.-K. Wang et al. / Ceramics International 38 (2012) 2829–2833 2831
heat treatment at 400 and 450 8C in O2 atmosphere. The band
gap energy can be calculated from Tauc’s law [25] using the
relation of (ahv)n = A(hv � Eg), where a is the absorption
coefficient, n is a characteristic constant depends on the
material, A is a constant, and Eg is the band gap energy of the
film. For the indirect allowed transition Nb-doped WO3 films, n
is equal to 2. The band gap energy of Nb-doped WO3 films are
1.98, 3.58, 3.69, and 3.69 eV for as-deposited state and
annealed films of 350, 400, and 450 8C, respectively. The
42403836343230
Inte
nsity
(arb
. uni
ts)
Binding Energy (eV)
experimental data fitting peaks sum background W+6 4f7/2
W+6 4f5/2
W+4 4f7/2
W+4 4f5/2
at as-deposit ed stateW 4f7/2&5/2
Binding Energy (eV) 42403836343230
after 450 oC heat-treatmentW 4f7/2&5/2
experimental data fitting peaks sum background W+6 4f7/2
W+6 4f5/2Inte
nsity
(arb
. uni
ts)
Fig. 4. The XPS spectra of W 4f7/2 and 5/2 and Nb 3d5/2 and 3/2 of Nb-doped W
variation of band gap energy could be caused by the increase of
chemical stoichiometry and crystal growth effect. The chemical
states of W and Nb atoms of as-deposited and annealed film at
450 8C are examined by XPS and the results shown in Fig. 4.
The W4f XPS spectra contain three major peaks at 33.2, 35.4
and 37.6 eV. Those peaks can be decomposed into two doublets
of W+6 (35.6, 37.7 eV) and W+4 (32.9, 35.1 eV) ions of W 4f7/2
and W4f5/2 [26]. The XPS spectra of Nb atom for as-deposited
state show two major peaks at 207.2 and 209.8 eV and a small
217215213211209207205203201
Inte
nsity
(arb
. uni
ts)
Binding Energy (eV)
Binding Energy (eV)
experimental data fitting peaks sum background Nb+5 3d5/2
Nb+5 3d3/2
Nb+2 3d5/2
Nb+2 3d3/2
at as-deposited stateNb 3d5/2&3/2
217215213211209207205203201
at af ter 450 oC heat treatentNb 3d5/2&3/2
experimental data fitting peaks sum background Nb+5 3d5/2
Nb+5 3d3/2
Inte
nsity
(arb
. uni
ts)
O3 films at as-deposited and after heat treatment at 450 8C in O2 atmosphere.
1.00.50.0-0.5-1.0-0.4
-0.3
-0.2
-0.1
0.0
0.1
0.2
as deposited state 450 oC heat-treated film
Cur
rent
Den
sity
(mA
/cm
2 )
Potential vs. SCE (volts)
Fig. 6. The cycle voltammogram of electrochromic films for as-deposited state
and 450 8C heat-treated of Nb-doped WO3 films.
110010009008007006005004003000
10
20
30
40
50
60
70
80
90
100
Tran
smitt
ance
(%)
Wavelength (nm)
as-depsotied bleach as-depsotied color 450 oC bleach 450 oC color
Fig. 5. The optical transmittance spectra of Nb-doped WO3 film at as-deposited
state and at heat-treated at 450 8C after bleach and color reaction.
C.-K. Wang et al. / Ceramics International 38 (2012) 2829–28332832
peak at 204.6 eV. Those XPS peaks are the superimposition of
the doublets of Nb+5 (207.4, 209.7 eV) and Nb+2 (204.4,
206.3 eV) ions for Nb 3d5/2 and Nb 3d3/2 [27]. From those
results, we can conclude that the chemical compositions in as-
deposited Nb-doped WO3 film are WO2, WO3, Nb2O5 and
small amount of NbO. It can be inferred that the Nb atom reacts
with oxygen of WO3 to form NbO and Nb2O5. On the other
hand, as XPS analysis was performed from the surface of 5 nm
depth film, the exposure of Nb-doped film in air may be another
reason for existence of large amount of Nb2O5. After annealing
treatment at 450 8C in O2 atmosphere the XPS spectra shows a
W4f7/2 and 5/2 doublet at 35.4 and 37.6 eV and a doublet Nb
3d5/2 and 3/2 at 207.2 and 209.8 eV, which is stoichiometric
chemical composition of WO3 and Nb2O5. The as-deposited
film and annealed film at 450 8C are colored at �1 V in LiClO4/
PC solution for 60 s.
The optical transmittance spectra of the films are shown in
Fig. 5. In the coloration reaction, the W+6 ions are reduced into
W+5 and the Nb+4 are reduced into Nb+4 to bring out the
electrochromic effect. For the as-deposited film, the optical
transmittance does not vary obviously before and after
electrochemical insertion of Li+ ions and the film color is
504540353025
W 4f7/2&5/2
after one insertion/extracion cycle
as-deposited state
Inte
nsity
(arb
uni
ts)
Binding Energy (eV)
Fig. 7. The XPS spectra of W4f and Nb 3d of Nb-doped WO3 films fo
still brown. The color of 450 8C annealed film becomes blue
after Li+ intercalation reaction at �1 V. The variation of optical
transmittance at bleach and color state of as-deposited and 350,
400, and 450 8C annealed films are 0.6, 19, 35, and 38.4% at
wavelength of 633 nm. The coloration efficiency of the films is
calculated using the equation of CE = DO.D./DQ. The DO.D is
the change of optical density and is equal to log(Tb/Tc), where
Tb and Tc are the optical transmittance at bleach and color state
at specific optical wavelength. DQ is the reacted charge density
in the color or bleach reaction. The coloration efficiencies at
633 nm are 4, 18.5, 22, and 23 C/cm2, respective for as-
deposited film and 350, 400, and 450 8C annealed films. The
increase of color efficiency with annealing temperature is due
to chemical stoichiometry of electrochromic films.
Cyclic voltammetry (CV) were measured for as-deposited
and 450 8C heat-treated films at the potential range of �1 to 1 V
in three electrodes configuration with scan speed of 50 mV/s
and the results are shown in Fig. 6. The CV loop of as-deposited
film has a larger area compared to that of 450 8C annealed film
and there are two pairs of cathodic/anodic current peaks. On the
other hand, the 450 8C annealed film has only one pair of
cathodic/anodic current peaks. However, in the Bathe’s study,
220215210205200195
Nb 3d5/2&3/2
Inte
nsity
(arb
uni
ts)
Binding Energy (eV)
as-deposited state
after one insertion/extracion cycle
r as-deposited state and that after one insertion/extraction reaction.
C.-K. Wang et al. / Ceramics International 38 (2012) 2829–2833 2833
they show only one pair of cathodic/anodic peak for 2% Nb–
WO3 films. In order to clarify the electrochemical mechanism
in the insertion/extraction reaction, we compare the XPS
spectra for as-deposited state and that after insertion/extraction
cycle, which are shown in Fig. 7. It clearly shows that the peak
intensity of W+4 and Nb+2 decrease after one insertion/
extraction cycle. We can reasonably infer that those two pairs of
cathodic/anodic peaks are consisted of the oxidation of WO2
and NbO into WO3 and Nb2O5.
4. Conclusion
The Nb-doping WO3 electrochromic films are prepared
successfully by electron beam method, where tungsten and
niobium atoms are well distributed. The as-deposited film is
amorphous and non-stoichiometric. The film does not show
obvious electrochromic effect and in CV cycling the WO2 and
NbO are oxidized into WO3 and Nb2O5. After post annealing in
O2 atmosphere, the film transforms into crystalline structure and
become chemically stoichiometric. The energy band gap and
electrochromic effect also increase with annealing temperature.
Acknowledgements
This work was supported by the National Science Council of
Taiwan under contract of NSC96-2218-E-006-006. Author
D.R. Sahu is also thankful to National Research Foundation,
South Africa for supporting this work.
References
[1] C.G. Granqvist, Handbook of Inorganic Electrochromic Materials, Else-
vier, 1995.
[2] S.K. Deb, A novel electrophotographic system, Appl. Opt. 3 (1969) 192–
195.
[3] K. Sauvet, L. Sauques, A. Rougier, Electrochromic properties of WO3 as a
single layer and in a full device: from the visible to the infrared, J. Phys.
Chem. Solids 71 (2010) 696–699.
[4] H. Razmi, R.M. Rezaei, Preparation of tungsten oxide nanoporous thin
film at carbon ceramic electrode for electrocatalytic applications, Elec-
trochim. Acta 56 (2011) 7220–7223.
[5] D.J. Taylor, J.P. Cronin, L.F. Allard,D.P. Birnie, Microstructure of laser-fired,
sol–gel-derived tungsten oxide films, Chem. Mater. 8 (1996) 1396–1401.
[6] K. Sauvet, L. Saugues, A. Rougier, IR electrochromic WO3 thin films:
from optimization to devices, Solar Energy Mater. Solar Cells 93 (2009)
2045–2049.
[7] O. Bohnke, G. Frand, M. Fromm, J. Weber, O. Greim, Depth profiling of
W, O and H in tungsten trioxide thin films using RBS and ERDA
techniques, Appl. Surf. Sci. 93 (1996) 45–52.
[8] I. Porqueras, E. Bertran, Optical properties of Li+ doped electrochromic
WO3 thin films, Thin Solid Films 377/378 (2000) 8–13.
[9] A. Georg, W. Graf, R. Neumann, V. Wittwer, Role of water in gasochromic
WO3 films, Thin Solid Films 384 (2001) 269–275.
[10] W.B. Henley, G.J. Sachs, Deposition of electrochromic tungsten oxide thin
films by plasma-enhanced chemical vapor deposition, J. Electrochem.
Soc. 144 (1997) 1045–1050.
[11] J. Zhang, X.L. Wang, X.H. Xia, C.D. Gu, J.P. Tu, Electrochromic behavior
of WO3 nanotree films prepared by hydrothermal oxidation, Solar Energy
Mater. Solar Cells 95 (2011) 2107–2112.
[12] W. Li, J. Li, X. Wang, S. Luo, J. Xiao, Q. Chen, Visible light photoelec-
trochemical responsiveness of self-organized nanoporous WO3 films,
Electrochim. Acta 56 (2010) 620–625.
[13] N. Ozer, Optical and electrochemical characteristics of sol–gel deposited
tungsten oxide films: a comparison, Thin Solid Films 304 (1997) 310–314.
[14] K. Yoshimura, T. Miki, S. Tanemura, Electrochromic properties of
niobium oxide thin films prepared by DC magnetron sputtering, J.
Electrochem. Soc. 144 (1997) 2982–2985.
[15] M.A.B. Gomes, L.O.S. Bulhoes, S.C. Castro, A.J. Damiao, Electrochemi-
cal and chromogenics kinetics of lithium intercalation in anodic niobium
oxide films, J. Electrochem. Soc. 137 (1990) 3067–3071.
[16] A.I. Gavrilyuk, Nanosized WO3 thin film as a multifunctional hydrogen
material for achieving photolysis in CuCl films via hydrogen photosensi-
tization, Solar Energy Mater. Solar Cells 94 (2010) 515–523.
[17] Dilek Isık, Metin Ak, Caner durucan, structural, electrochemical and
optical comparisons of tungsten oxide coatings derived from tungsten
powder-based sols, Thin Solid Films 518 (2009) 104–111.
[18] M. Deepa, A.K. Srivastava, S.N. Sharma, Govind, S.M. Shivaprasad,
Microstructural and electrochromic properties of tungsten oxide thin films
produced by surfactant mediated electrodeposition, Appl. Surf. Sci. 254
(2008) 2342–2352.
[19] A. Rougier, A. Blyr, J. Garcia, Q. Zhang, S.A. Impey, Electrochromic W–
M–O (M = V, Nb) sol–gel thin films: a way to neutral colour, Solar Energy
Mater. Solar Cells 71 (2002) 343–357.
[20] T. Ivanova, K.A. Gesheva, M. Kalitzova, B. Marsen, B. Cole, E.L. Miller,
Electrochromic behavior of Mo/W oxides related to their surface mor-
phology and intercalation process parameters, Mater. Sci. Eng. B 142
(2007) 126–134.
[21] S.R. Bathe, P.S. Patil, Influence of Nb doping on the electrochromic
properties of WO3 films, J. Phys. D: Appl. Phys. 40 (2007) 7423–7431.
[22] S. Hashimoto, H. Matsuoka, Lifetime of electrochromism of amorphous
WO3–TiO2 thin films, J. Electrochem. Soc. 138 (1991) 2403–2408.
[23] A.K. Chawla, S. Singhal, H.O. Gupta, R. Chandra, Influence of nitrogen
doping on the sputter-deposited WO3 films, Thin Solid Films 518 (2009)
1430–1433.
[24] C.O. Avellaneda, L.O.S. Bulhoes, Intercalation in WO3 and WO3: Li
films, Solid State Ionics 165 (2003) 59–64.
[25] K.N. Narayanan Unni, Optical characterization of europium diphthalo-
cyanine thin films, Mater. Lett. 57 (2003) 2215–2218.
[26] G. Leftheriotis, S. Papaefthimiou, P. Yianoulis, A. Siokou, Effect of the
tungsten oxidation states in the thermal coloration and bleaching of
amorphous WO3 films, Thin Solid films 384 (2001) 298–306.
[27] M. Ziolek, I. Nowak, Characterization techniques employed in the study
of niobium and tantalum-containing materials, Catal. Today 78 (2003)
543–553.